WO2022042731A1 - Acier à forte expansion de trou en bainite de qualité 980 mpa et procédé de fabrication de celui-ci - Google Patents

Acier à forte expansion de trou en bainite de qualité 980 mpa et procédé de fabrication de celui-ci Download PDF

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Publication number
WO2022042731A1
WO2022042731A1 PCT/CN2021/115433 CN2021115433W WO2022042731A1 WO 2022042731 A1 WO2022042731 A1 WO 2022042731A1 CN 2021115433 W CN2021115433 W CN 2021115433W WO 2022042731 A1 WO2022042731 A1 WO 2022042731A1
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Prior art keywords
high hole
content
steel
steel according
980mpa
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PCT/CN2021/115433
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English (en)
Chinese (zh)
Inventor
王焕荣
杨峰
张晨
杨阿娜
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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Application filed by Baoshan Iron and Steel Co Ltd filed Critical Baoshan Iron and Steel Co Ltd
Priority to US18/043,267 priority Critical patent/US20230313333A1/en
Priority to JP2023513802A priority patent/JP7829558B2/ja
Priority to KR1020237009928A priority patent/KR20230059810A/ko
Priority to EP21860563.2A priority patent/EP4206351A4/fr
Publication of WO2022042731A1 publication Critical patent/WO2022042731A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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    • C23G3/02—Apparatus for cleaning or pickling metallic material for cleaning wires, strips, filaments continuously
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
    • C23G1/08—Iron or steel

Definitions

  • the invention relates to the field of high-strength steel, in particular to a 980MPa-grade bainite high hole-expanding steel and a manufacturing method thereof.
  • the lightweight of passenger cars is not only the development trend of the automobile industry, but also the requirements of laws and regulations.
  • the fuel consumption is stipulated in the laws and regulations, in fact, it is a disguised requirement to reduce the weight of the body, which is reflected in the requirement of high strength, thinning and light weight.
  • High-strength weight reduction is an inevitable requirement for subsequent new models, which will inevitably lead to higher steel grades and changes in the chassis structure.
  • the requirements for material properties, surfaces, and molding technologies will be improved, such as Hydroforming, hot stamping, laser welding, etc., and then transform the material's high strength, stamping, flanging, springback and fatigue properties.
  • the development of domestic high-strength and high-hole-expanding steel not only has a relatively low strength level, but also has poor performance stability.
  • the high-hole-expansion steel used by domestic auto parts companies is basically high-strength steel with a tensile strength below 600MPa, and the competition for high-hole-expansion steel below 440MPa is fierce.
  • the high hole-expanding steel with a tensile strength of 780MPa is gradually being used in batches, but higher requirements are also put forward for the two important indicators of elongation and hole expansion.
  • the 980MPa-level high hole-expanding steel is still in the stage of R&D and certification, and has not yet reached the stage of mass use.
  • the hole expansion ratio of a material is closely related to many factors, the most important factors include the uniformity of the structure, the level of inclusion and segregation control, the different structure types, and the measurement of the hole expansion ratio.
  • a single homogeneous structure is beneficial to obtain a higher hole expansion ratio, while a dual-phase or multi-phase structure is usually not conducive to the improvement of the hole expansion ratio.
  • the purpose of the present invention is to provide a 980MPa grade bainite high hole-enlarging steel and a manufacturing method thereof.
  • the yield strength of the high-hole-enlarging steel is greater than or equal to 800MPa, the tensile strength is greater than or equal to 980MPa, and at the same time, it has good elongation (transverse A 50 ⁇ 11%) and hole expansion performance (hole expansion rate ⁇ 40%), it can be used in parts of passenger car chassis such as control arms and subframes that require high strength and thinning.
  • the technical scheme of the present invention is:
  • the composition design of the present invention adopts a lower C content, which can ensure that the user has excellent weldability during use, and ensures that the obtained martensite structure has good hole expansion and impact toughness;
  • the lower the carbon content the better;
  • the higher Si content is designed to match the process to obtain more retained austenite, thereby improving the plasticity of the material;
  • the higher Si content is conducive to reducing the unrecrystallized steel temperature, so that the steel can complete the dynamic recrystallization process in a wide range of finishing rolling temperature, thereby improving the structural anisotropy of the steel, refining the austenite grains and the final bainite lath size, improving the plasticity and hole expansion ratio.
  • the 980MPa grade bainite high hole-expanding steel according to the present invention has the following chemical composition weight percentages: C 0.05-0.10%, Si 0.5-2.0%, Mn 1.0%-2.0%, P ⁇ 0.02%, S ⁇ 0.003%, Al 0.02 ⁇ 0.08%, N ⁇ 0.004%, Mo ⁇ 0.1%, Ti 0.01 ⁇ 0.05%, Cr ⁇ 0.5%, B ⁇ 0.002%, O ⁇ 0.0030%, the rest are Fe and other inevitable impurities.
  • the 980MPa grade bainite high hole expanding steel according to the present invention also contains one or more elements selected from Nb ⁇ 0.06%, V ⁇ 0.05%, Cu ⁇ 0.5%, Ni ⁇ 0.5% and Ca ⁇ 0.005% .
  • the content of Mo by weight is 0.1-0.55%.
  • the 980MPa grade bainite high hole-expanding steel according to the present invention has the following chemical composition weight percentages: C 0.05-0.10%, Si 0.5-2.0%, Mn 1.0%-2.0%, P ⁇ 0.02% , S ⁇ 0.003%, Al 0.02 ⁇ 0.08%, N ⁇ 0.004%, Mo ⁇ 0.1%, Ti 0.01 ⁇ 0.05%, Cr ⁇ 0.5%, B ⁇ 0.002%, O ⁇ 0.0030%, Nb ⁇ 0.06%, V ⁇ 0.05%, Cu ⁇ 0.5%, Ni ⁇ 0.5%, Ca ⁇ 0.005%, the rest are Fe and other inevitable impurities, and the 980MPa grade bainite high hole expanding steel contains Nb, V, Cu, Ni and Ca. At least one of Cr and B, preferably at least one or both of Cr and B.
  • the Nb and V contents are preferably ⁇ 0.03%, respectively; the Cu and Ni contents are preferably ⁇ 0.3%, respectively, and the Ca content is preferably ⁇ 0.002%.
  • the yield strength of the 980MPa grade bainitic high hole-expanding steel according to the present invention is ⁇ 800MPa, preferably ⁇ 830MPa, more preferably ⁇ 850MPa, tensile strength ⁇ 980MPa, preferably ⁇ 1000MPa, more preferably ⁇ 1020MPa, transverse direction A 50 ⁇ 11%, hole expansion ratio ⁇ 40%, preferably ⁇ 50%.
  • the microstructure of the 980MPa grade bainite high hole expanding steel according to the present invention is bainite + retained austenite.
  • the content of retained austenite in the 980MPa grade bainite high hole-expanding steel is 1-5%.
  • composition design of the high hole-expanding steel of the present invention is the composition design of the high hole-expanding steel of the present invention:
  • Carbon the basic element in steel, is also one of the important elements in the present invention. Carbon expands the austenite phase region and stabilizes the austenite. As an interstitial atom in steel, carbon plays a very important role in improving the strength of steel, and has the greatest impact on the yield strength and tensile strength of steel.
  • the structure to be obtained is low-carbon bainite, in order to obtain a high-strength steel with a tensile strength of 980MPa, the carbon content must be guaranteed to be above 0.05%, otherwise the carbon content is below 0.05%, even if fully quenched Even at room temperature, its tensile strength cannot reach 980MPa; however, the carbon content cannot be higher than 0.10%.
  • the carbon content should be controlled between 0.05-0.10%, preferably in the range of 0.06-0.08%.
  • Silicon the basic element in steel, is also one of the important elements in the present invention.
  • the increase of Si content not only improves the solid solution strengthening effect, but also plays the following two roles more importantly.
  • the non-recrystallization temperature of the steel is greatly reduced, so that the steel can complete dynamic recrystallization in a wide temperature range.
  • the final rolling temperature can be rolled within the final rolling temperature range of 800-920 °C, so that the difference between the transverse and longitudinal microstructures is reduced, which is not only conducive to improving the strength and plasticity, but also conducive to obtaining good
  • Another important role of Si is to inhibit the precipitation of cementite, and under appropriate rolling process conditions, especially when obtaining a structure dominated by bainite, a certain amount of retained austenite can be retained , which is beneficial to increase the elongation.
  • This effect of Si must be manifested when its content reaches more than 0.5%; but the content of Si should not be too high, otherwise the rolling force load during the actual rolling process is too large, which is not conducive to the stable production of products. Therefore, the content of Si in the steel is usually controlled between 0.5-2.0%, and the preferred range is between 0.8-1.6%.
  • Manganese the most basic element in steel, is also one of the most important elements in the present invention.
  • Mn is an important element to expand the austenite phase region, which can reduce the critical cooling rate of steel, stabilize austenite, refine grains, and delay the transformation of austenite to pearlite.
  • the effect of molybdenum on the delay of ferrite and pearlite and the reduction of the critical cooling rate is much greater than that of manganese.
  • the content of manganese in the steel can be appropriately reduced, and should generally be controlled at more than 1.0%; at the same time, the content of Mn should generally not exceed 2.0%, otherwise Mn segregation is likely to occur during steelmaking, and heat is also likely to occur during continuous slab casting. crack. Therefore, the content of Mn in the steel is generally controlled at 1.0-2.0%, preferably in the range of 1.4-1.8%.
  • Phosphorus is an impurity element in steel. P is easy to segregate on the grain boundary. When the content of P in the steel is high ( ⁇ 0.1%), Fe 2 P is formed to precipitate around the grain, reducing the plasticity and toughness of the steel, so the lower the content, the better. It is better to control within 0.02% without increasing the cost of steelmaking.
  • Sulfur is an impurity element in steel.
  • S in steel usually combines with Mn to form MnS inclusions, especially when the content of S and Mn is high, more MnS will be formed in the steel, and MnS itself has a certain plasticity.
  • the deformation in the rolling direction not only reduces the transverse plasticity of the steel, but also increases the anisotropy of the structure, which is unfavorable for the hole expansion performance. Therefore, the lower the S content in the steel, the better.
  • the Mn content in the present invention must be at a higher level, in order to reduce the MnS content, the S content should be strictly controlled, and the S content should be controlled within 0.003%.
  • the preferable range is 0.0015% or less.
  • the role of aluminum in steel is mainly deoxidation and nitrogen fixation.
  • the main role of Al is to deoxidize and refine grains.
  • the content of Al is usually controlled at 0.02-0.08%; if the content of Al is less than 0.02%, it cannot achieve the effect of refining grains; similarly, When the Al content is higher than 0.08%, the grain refinement effect is saturated. Therefore, the content of Al in the steel can be controlled between 0.02-0.08%, and the preferred range is between 0.02-0.05%.
  • Nitrogen is an impurity element in the present invention, and the lower the content, the better. But nitrogen is an inevitable element in the steelmaking process. Although its content is small, when combined with strong carbide forming elements such as Ti, the formed TiN particles have a very adverse effect on the properties of the steel, especially on the hole expansion performance. Due to the square shape of TiN, there is a large stress concentration between its sharp corners and the matrix. During the process of hole expansion and deformation, the stress concentration between TiN and the matrix is easy to form cracks, thereby greatly reducing the hole expansion performance of the material. Under the premise of controlling the nitrogen content as much as possible, the lower the content of strong carbide-forming elements such as Ti, the better. In the present invention, a trace amount of Ti is added to fix nitrogen, so as to minimize the adverse effects brought by TiN. Therefore, the nitrogen content should be controlled below 0.004%, preferably below 0.003%.
  • Titanium is one of the important elements in the present invention. Ti mainly plays two roles in the present invention: one is to combine with the impurity element N in the steel to form TiN, which plays a part of "fixing nitrogen”; the other is to form a certain amount of finely dispersed TiN in the subsequent welding process of the material , suppress the austenite grain size, refine the structure and improve the low temperature toughness. Therefore, the content of Ti in the steel is controlled in the range of 0.01-0.05%, preferably in the range of 0.01-0.03%.
  • Molybdenum is one of the important elements in the present invention.
  • the addition of molybdenum to the steel can greatly delay the transformation of ferrite and pearlite, which is beneficial to obtain bainite structure in the middle and high temperature range; at the same time, the addition of molybdenum can also improve the stability of the structure and properties of the steel and refine the grains.
  • This effect of molybdenum is beneficial to the adjustment of various processes in the actual rolling process. For example, after the end of the final rolling, it can be cooled in stages, or it can be air-cooled first and then water-cooled. In the present invention, two methods of air cooling after rolling or direct cooling are adopted.
  • the addition of molybdenum can on the one hand ensure that structures such as ferrite or pearlite will not be formed during the air cooling process;
  • the dynamic recovery of the deformed austenite during the process is beneficial to improve the uniformity of the structure and properties, and is beneficial to the hole expansion performance.
  • the effect of molybdenum on inhibiting the formation of ferrite and pearlite requires its content to be more than 0.10%. Therefore, the content of molybdenum should be controlled at ⁇ 0.10%, and the preferred range is ⁇ 0.15%. In some embodiments, the molybdenum content is 0.1-0.55%.
  • Chromium is one of the important elements in the present invention.
  • chromium is not used to improve the hardenability of steel, but to combine with B, which is conducive to the formation of acicular ferrite structure in the welding heat-affected zone after welding, which can greatly improve the low-temperature toughness of the welding heat-affected zone.
  • the final application parts involved in the present invention are passenger car chassis products, the low temperature toughness of the welded heat affected zone is an important indicator. In addition to ensuring that the strength of the welding heat-affected zone cannot be reduced too much, the low-temperature toughness of the welding heat-affected zone must also meet certain requirements.
  • chromium itself also has a certain resistance to welding softening. Therefore, a small amount of chromium element needs to be added to the steel, the range of which is generally ⁇ 0.5%, such as 0.1-0.5%, and the preferred range is 0.2-0.4%.
  • the role of boron in steel is mainly to segregate at the austenite grain boundary to inhibit the formation of pro-eutectoid ferrite; the addition of boron to steel can also greatly improve the hardenability of steel.
  • the main purpose of adding trace boron is not to improve the hardenability, but to combine with chromium to improve the structure of the welding heat-affected zone and obtain acicular ferrite structure with good toughness.
  • the addition of boron element in steel is generally controlled below 0.002%, and the preferred range is between 0.0005-0.0015%.
  • Calcium is an addable element in the present invention.
  • Calcium can improve the morphology of sulfides such as MnS, so that elongated sulfides such as MnS become spherical CaS, which is beneficial to improve the morphology of inclusions, thereby reducing the adverse effect of elongated sulfides on hole expansion performance.
  • the addition of calcium oxide will increase the amount of calcium oxide, which is detrimental to the hole expansion performance. Therefore, the addition amount of steel grade calcium is usually ⁇ 0.005%, and the preferred range is ⁇ 0.002%.
  • Oxygen is an unavoidable element in the steelmaking process.
  • the content of O in the steel can generally reach below 30 ppm after deoxidation, which will not cause obvious adverse effects on the performance of the steel plate. Therefore, it is sufficient to control the O content in the steel within 30 ppm.
  • Niobium is one of the elements that can be added in the present invention. Similar to titanium, niobium is a strong carbide element in steel. The addition of niobium to steel can greatly increase the unrecrystallized temperature of steel. In the finishing rolling stage, deformed austenite with higher dislocation density can be obtained. In the subsequent transformation process The final phase transition structure can be refined. However, the addition amount of niobium should not be too much. On the one hand, the addition amount of niobium exceeds 0.06%, which is easy to form relatively coarse carbonitrides of niobium in the structure, which consumes some carbon atoms and reduces the precipitation strengthening effect of carbides.
  • the high content of niobium also easily causes the anisotropy of the hot-rolled austenite structure, which is inherited to the final structure in the subsequent cooling transformation process, which is detrimental to the hole expansion performance. Therefore, the niobium content in the steel is usually controlled to be ⁇ 0.06%, and the preferred range is ⁇ 0.03%.
  • Vanadium is an addable element in the present invention. Like titanium and niobium, vanadium is also a strong carbide former. However, the carbides of vanadium have a low solid solution or precipitation temperature, and are usually all dissolved in austenite in the finishing rolling stage. It is only when the temperature is lowered that the phase transformation begins that vanadium begins to form in the ferrite. Since the solid solubility of vanadium carbides in ferrite is greater than that of niobium and titanium, the size of vanadium carbides formed in ferrite is relatively large, which is not conducive to precipitation strengthening and contributes far to the strength of steel.
  • the addition amount of vanadium in steel is usually ⁇ 0.05%, and the preferred range is ⁇ 0.03%.
  • Copper is an additive element in the present invention. Adding copper to steel can improve the corrosion resistance of steel. When it is added together with P element, the corrosion resistance effect is better; to a strong precipitation strengthening effect. However, the addition of Cu is easy to form the phenomenon of "Cu embrittlement" during the rolling process. In order to make full use of the effect of improving the corrosion resistance of Cu in some applications, and at the same time not cause significant "Cu embrittlement" phenomenon, usually Cu The content of the element is controlled within 0.5%, preferably within 0.3%.
  • Nickel is an additive element in the present invention.
  • the addition of nickel to steel has certain corrosion resistance, but the corrosion resistance effect is weaker than that of copper.
  • the addition of nickel to steel has little effect on the tensile properties of steel, but it can refine the structure and precipitation of steel, and greatly improve the low temperature toughness of steel. ; At the same time, adding a small amount of nickel can inhibit the occurrence of "Cu brittleness" in the steel added with copper.
  • the addition of higher nickel has no obvious adverse effect on the properties of the steel itself. If copper and nickel are added at the same time, it can not only improve the corrosion resistance, but also refine the structure and precipitation of the steel, greatly improving the low temperature toughness. But since copper and nickel are both relatively precious alloying elements. Therefore, in order to minimize the cost of alloy design, the addition amount of nickel is usually ⁇ 0.5%, and the preferred range is ⁇ 0.3%.
  • the manufacturing method of the 980MPa grade bainite high hole expanding steel according to the present invention comprises the following steps:
  • Rolling temperature 950 ⁇ 1100°C, under 3-5 passes above 950°C, and the accumulated deformation is ⁇ 50%, preferably ⁇ 60%, the main purpose is to refine the austenite grains; to 920-950°C, and then carry out the last 3-7 passes of rolling and the accumulated deformation is ⁇ 70%, preferably ⁇ 85%; the final rolling temperature is 800-920°C;
  • Air-cooling for 0-10s is performed first to perform dynamic recovery to make the deformed austenite more uniform, and then the strip is cooled to 400-550°C and coiled at a cooling rate of ⁇ 10°C/s, preferably ⁇ 30°C/s. Cool down to room temperature naturally after coiling;
  • the operating speed of strip pickling is adjusted within the range of 30-100m/min, the pickling temperature is controlled between 75-85°C, and the tensile correction rate is controlled within ⁇ 2% to reduce the loss of strip elongation, and then rinse, The strip surface is dried and oiled.
  • rinsing is performed at a temperature range of 35-50° C. to ensure the surface quality of the strip, and the surface of the strip is dried and oiled between 120-140° C.
  • the innovation of the present invention is:
  • the composition design of the present invention adopts a lower C content, which can ensure that the user has excellent weldability during use, and ensures that the obtained martensite structure has good hole expansion and impact toughness;
  • the lower the carbon content the better;
  • the higher Si content is designed to match the process to obtain more retained austenite, thereby improving the plasticity of the material;
  • the higher Si content is conducive to reducing the unrecrystallized steel temperature, so that the steel can complete the dynamic recrystallization process in a wide range of finishing rolling temperature, thereby improving the structural anisotropy of the steel, refining the austenite grains and the final bainite lath size, improving the plasticity and hole expansion ratio.
  • the design idea of low-carbon bainite is adopted, and high silicon is added to inhibit and reduce the formation of cementite, and at the same time, the non-recrystallization temperature is reduced, and the temperature range of final rolling is expanded.
  • direct cooling or air cooling for a certain period of time
  • a bainite structure with fine and uniform grains can be obtained, and a small amount of retained austenite is contained at the same time.
  • the bainite structure gives the steel sheet higher strength, while the retained austenite gives the steel sheet higher ductility.
  • the combination of the two can make the steel sheet show good matching of strength, ductility and hole expansion ratio.
  • the rhythm of the rolling process should be completed as quickly as possible.
  • air-cooled for a certain period of time and then water-cooled or directly water-cooled.
  • the main purpose of air cooling Due to the inclusion of a certain amount of manganese and molybdenum in the composition design, manganese is an element that stabilizes austenite, while molybdenum greatly delays the transformation of ferrite and pearlite, while promoting the transformation of bainite. Therefore, in the short-time air cooling process, the rolled deformed austenite will not undergo phase transformation, that is, the ferrite structure will not be formed, but a dynamic recovery process will occur.
  • the dislocations inside the austenite grains will be greatly reduced, the austenite structure will be more uniform, and the bainite structure formed in the subsequent transformation process will be more uniform.
  • the water cooling rate of the strip is required to be ⁇ 10°C/s.
  • the strip steel needs to be cooled to the bainite transformation temperature range.
  • the bainite transformation temperature range is 400-550°C.
  • the bainitic lath becomes smaller, the structure is relatively more uniform, the strength increases and the plasticity decreases; on the contrary, as the coiling temperature increases, the bainitic lath in the structure decreases.
  • the body can be partially transformed into granular bainite, resulting in a decrease in strength and an increase in plasticity.
  • Theoretical calculations and experiments have confirmed that the bainite structure with excellent comprehensive properties can be obtained when the strip is cooled to the range of 400-550 °C.
  • the coiling temperature is ⁇ 550°C
  • relatively coarse upper bainite will be formed in the structure, which cannot meet the strength requirement above 980MPa; when the coiling temperature is ⁇ 400°C, the structure will be transformed into martensite.
  • the coiling temperature needs to be controlled between 400-550 °C. It is precisely based on this innovative composition and process design idea that the present invention can obtain 980MPa-level high hole-expanding steel with excellent strength, plasticity and hole-expanding performance. After coiling, the steel coil is naturally cooled slowly, and the microstructure of bainite + retained austenite can be obtained.
  • the cooling rate of natural slow cooling is less than or equal to 20°C/h, preferably less than or equal to 15°C/h.
  • the steel coil or steel plate has excellent matching of strength, plasticity and hole expansion and flanging, its yield strength is ⁇ 800MPa, tensile strength is ⁇ 980MPa, and it has good elongation (transverse A 50 ⁇ 11%) and expansion.
  • Hole performance (hole expansion ratio ⁇ 40%), it can be used in the manufacture of parts such as automobile chassis and sub-frames that require high-strength thinning and hole-enlarging and flanging, and has a very broad application prospect.
  • FIG. 1 is a process flow diagram of the method for manufacturing 980MPa grade bainite high hole-expanding steel according to the present invention.
  • FIG. 2 is a schematic diagram of the rolling process in the manufacturing method of 980MPa grade bainite high hole-expanding steel according to the present invention.
  • FIG. 3 is a schematic diagram of the cooling process in the manufacturing method of the 980MPa grade bainite high hole-expanding steel according to the present invention.
  • FIG. 4 is a photo of a typical metallographic structure of Example 2 of the 980MPa grade bainite high hole-expanding steel according to the present invention.
  • FIG. 5 is a photo of typical metallographic structure of Example 4 of the 980MPa grade bainite high hole-expanding steel according to the present invention.
  • FIG. 6 is a photo of a typical metallographic structure of Example 6 of the 980MPa grade bainite high hole-expanding steel according to the present invention.
  • FIG. 7 is a photo of typical metallographic structure of Example 8 of the 980MPa grade bainite high hole-expanding steel according to the present invention.
  • the manufacturing method of 980MPa grade bainite high hole expanding steel according to the present invention includes the following steps:
  • Rolling temperature 950 ⁇ 1100°C, under 3-5 passes above 950°C and the accumulated deformation is ⁇ 50%, then the intermediate billet is warmed to 920-950°C, and then the last 3-7 passes are rolled and the accumulated deformation is ⁇ 70%; the final rolling temperature is 800-920°C;
  • the operating speed of strip pickling is adjusted within the range of 30-100m/min, the pickling temperature is controlled between 75-85°C, the pull-straightening rate is controlled within ⁇ 2%, the rinsing is carried out in the temperature range of 35-50°C, and the Dry the surface between 120-140°C and apply oil.
  • Tables 1-3 are the production process parameters of the steel embodiments of the present invention for the composition of the high hole-enlarging steel embodiments of the present invention, wherein the thickness of the billet in the rolling process is 120 mm;
  • Table 4 is the mechanical properties of the steel plates of the embodiments of the present invention.
  • the tensile properties yield strength, tensile strength, elongation
  • the hole expansion ratio was tested according to the ISO16630-2017 international standard.
  • the yield strength of the steel coil is ⁇ 800MPa
  • the tensile strength is ⁇ 980MPa
  • the elongation is between 10-13%
  • the hole expansion rate is ⁇ 40%.
  • Figures 4 to 7 show typical metallographic photographs of Examples 2, 4, 6 and 8, respectively. It can be seen that the typical microstructure is bainite with a small amount of retained austenite.
  • the 980MPa high hole expanding steel of the present invention has good matching of strength, plasticity and hole expanding performance, and is especially suitable for parts such as automobile chassis structures that require high strength thinning and hole expanding and flanging forming, such as control arms It can also be used for parts that need to be turned, such as wheels, and has broad application prospects.

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Abstract

L'invention concerne un acier à forte expansion de trou en bainite de qualité 980 MPa et un procédé de fabrication de celui-ci. L'acier contient les composants chimiques suivants, exprimés en pourcentage massique : 0,05-0,10% de C, 0,5-2,0% de Si, 1,0-2,0% de Mn, P≤0,02％, S≤0,003％, 0,02-0,08% d'Al, N≤0,004％, Mo≥0,1％, 0,01-0,05% de Ti, Cr≤0,5％, B≤0,002％, O≤0,0030％, et le restant étant du Fe et d'autres impuretés inévitables. L'acier à forte expansion de trou selon la présente invention présente une limite d'élasticité de ≥ 800 MPa et une résistance à la traction de ≥ 980MPa, présente un bon taux d'allongement (le A50 transversal étant ≥ 11％) et des bonnes performances d'expansion de trou (le taux d'expansion de trou étant ≥ 40％), et peut être appliqué à une position sur une partie de châssis d'un véhicule de tourisme, telle qu'un bras de commande et un cadre d'étau, où une résistance élevée et un amincissement sont exigés.
PCT/CN2021/115433 2020-08-31 2021-08-30 Acier à forte expansion de trou en bainite de qualité 980 mpa et procédé de fabrication de celui-ci Ceased WO2022042731A1 (fr)

Priority Applications (4)

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US18/043,267 US20230313333A1 (en) 2020-08-31 2021-08-30 980 mpa-grade bainite high hole expansion steel and manufacturing method therefor
JP2023513802A JP7829558B2 (ja) 2020-08-31 2021-08-30 ９８０ＭＰａレベルのベイナイト高穴拡げ性鋼及びその製造方法
KR1020237009928A KR20230059810A (ko) 2020-08-31 2021-08-30 980MPa급의 구멍 확장성이 높은 베이나이트강 및 이의 제조 방법
EP21860563.2A EP4206351A4 (fr) 2020-08-31 2021-08-30 Acier à forte expansion de trou en bainite de qualité 980 mpa et procédé de fabrication de celui-ci

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CN202010897959.5A CN114107798A (zh) 2020-08-31 2020-08-31 一种980MPa级贝氏体高扩孔钢及其制造方法
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CN114892080A (zh) * 2022-04-27 2022-08-12 鞍钢股份有限公司 一种720MPa级析出强化型热轧贝氏体钢及其生产方法
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WO2024111526A1 (fr) * 2022-11-22 2024-05-30 Ｊｆｅスチール株式会社 Tôle en acier laminée à chaud hautement résistante, et procédé de fabrication de celle-ci
WO2024111527A1 (fr) * 2022-11-22 2024-05-30 Ｊｆｅスチール株式会社 Tôle en acier laminée à chaud hautement résistante, et procédé de fabrication de celle-ci
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CN114774788A (zh) * 2022-04-25 2022-07-22 马鞍山钢铁股份有限公司 一种900MPa级高表面质量的酸洗汽车用钢及其制造方法和应用
CN114774788B (zh) * 2022-04-25 2023-08-29 马鞍山钢铁股份有限公司 一种900MPa级高表面质量的酸洗汽车用钢及其制造方法和应用
CN114892080A (zh) * 2022-04-27 2022-08-12 鞍钢股份有限公司 一种720MPa级析出强化型热轧贝氏体钢及其生产方法
CN117305692A (zh) * 2022-06-22 2023-12-29 宝山钢铁股份有限公司 一种高扩孔钢及其制造方法
CN115647036A (zh) * 2022-10-10 2023-01-31 唐山不锈钢有限责任公司 一种700MPa级热轧带钢及其生产方法
WO2024111526A1 (fr) * 2022-11-22 2024-05-30 Ｊｆｅスチール株式会社 Tôle en acier laminée à chaud hautement résistante, et procédé de fabrication de celle-ci
WO2024111527A1 (fr) * 2022-11-22 2024-05-30 Ｊｆｅスチール株式会社 Tôle en acier laminée à chaud hautement résistante, et procédé de fabrication de celle-ci
JP7522979B1 (ja) * 2022-11-22 2024-07-26 Ｊｆｅスチール株式会社 高強度熱延鋼板及びその製造方法
JP7522980B1 (ja) * 2022-11-22 2024-07-26 Ｊｆｅスチール株式会社 高強度熱延鋼板及びその製造方法
EP4600395A4 (fr) * 2022-11-22 2025-12-17 Jfe Steel Corp Tôle en acier laminée à chaud hautement résistante, et procédé de fabrication de celle-ci
EP4600396A4 (fr) * 2022-11-22 2026-01-14 Jfe Steel Corp Tôle en acier laminée à chaud hautement résistante, et procédé de fabrication de celle-ci
CN118291854A (zh) * 2024-03-25 2024-07-05 马鞍山钢铁股份有限公司 一种低成本高成形性能抗拉强度450MPa级酸洗高强钢及其制造方法和应用

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CN114107798A (zh) 2022-03-01
JP7829558B2 (ja) 2026-03-13

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